CN106435379B - 550MPa grades of special the thickness easily anti-lamellar tearing steel plate of welding high tenacity and its manufacturing method - Google Patents
550MPa grades of special the thickness easily anti-lamellar tearing steel plate of welding high tenacity and its manufacturing method Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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Abstract
The present invention relates to a kind of 550MPa grades special thick easily welding anti-lamellar tearing steel plates of high tenacity, manufacturing process flow: the techniques such as KR molten iron pretreatment-converter smelting-LF refining-RH vacuum outgas-continuous casting-continuous casting billet covering slow cooling-continuous casting billet inspection cleaning-slab heating-high-pressure water descaling-rolling-aligning-steel plate heap slow cooling-quenching-tempering, finished product thickness are the steel plate of 70mm and 120mm.This invention takes Ultra-low carbon+a small amount of Ni and Mo ingredient design, the modifier treatment technique of quenching+tempering is used to obtain bigger thickness steel plate and better low-temperature impact toughness in the case where guaranteeing carbon equivalent and cooling cracks the susceptible index number in technique.
Description
Technical field
The invention belongs to technical field of ferrous metallurgy, and in particular to a kind of 550MPa grades of easy welding super-thick steel plate.
Background technique
Yield strength is greater than 550MPa grade high-strength high tenacity super-thick steel plate and is widely used in the large sizes such as marine worker, nuclear power, water power
In structural steelwork, and key position is used for as main load-bearing steel plate.In design, high intensity and high ductility is not only required
Property, for the safety for guaranteeing engineering, it is also necessary to have good easy weldability and anti-lamellar tearing performance.Not with material property
The disconnected increase promoted with engineering difficulty, more stringent requirements are proposed for weldability and low-temperature impact toughness to material, especially most
Super-thick steel plate of the big thickness to 120mm, it is desirable that yield strength >=550MPa, carbon equivalent≤0.55, cooling cracks the susceptible index number≤
0.24, -60 DEG C of low-temperature impact work >=100J or more.Such steel plate country has not been reported at present.
The patent of invention of 102191430 A of patent announcement CN proposes a kind of surrender 550MPa and easily welds high-strength and high ductility
Property steel plate and its manufacturing method, pass through cooling controlling and rolling controlling process, production thickness is less than or equal to the easy welding super-thick steel plate of 100mm, Pcm
Value≤0.19, -20 DEG C of Charpy-V impact power >=150J have no the description of 120mm thickness He -60 DEG C of low-temperature impact toughness.
Patent announcement number number CN101230444 uses controlled rolling and controlled cooling+tempering process, provide a kind of yield strength >=
570MPa, tensile strength >=690MPa, -20 DEG C of low-temperature impact toughness >=120J steel plates have no thickness description and -60 DEG C of low temperature
Toughness description.
Patent announcement CN101787489A uses the technique of controlled rolling and controlled cooling, provides a kind of yield strength >=550MPa, resists
Tensile strength >=670MPa, -40 DEG C of low-temperature impact toughness >=200J steel plates and its manufacturing method.It is not involved with -60 DEG C of low temperature
The manufacturing method of impact flexibility and 120mm thickness steel plate.
In the prior art, the steel plate of 550MPa rank, to obtain the characteristic easily welded, (carbon equivalent is small less than 0.55, Pcm
In 0.24), then the thickness of steel plate can not also surmount 100mm.
Summary of the invention
The technical problem to be solved by the present invention is to provide one kind for the above-mentioned prior art to use under the conditions of -60 DEG C
Thickness up to 120mm, yield strength 550MPa or more, carbon equivalent≤0.55, cold crack sensitivity coefficient (Pcm)≤0.24
The easily anti-lamellar tearing steel plate of welding high-strength and high-ductility and its manufacturing method.
The present invention solves the above problems used technical solution are as follows: a kind of 550MPa grades of special thick easily welding anti-layer of high tenacity
Shape tears steel plate, and the steel plate is basic element with Fe, and includes the chemical component of following mass percent: C 0.05-
0.08%, Si 0.2-0.4%, Mn 1.4-1.6%, Al 0.02-0.04%, Nb 0.01-0.03%, V 0.03-0.05%, Cr
0.3-0.5%, Ni 0.6-0.8%, Mo 0.2-0.4%, Ti 0.01-0.02%, B 0.001-0.002%, P≤0.015%, S≤
0.003%, N≤0.007%, carbon equivalent≤0.55, surplus are inevitable impurity, weld crack sensitivity coefficient Pcm=C+Si/
30+ (Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B≤0.24, steel plate with a thickness of 70-120mm.
The mechanical property of steel plate of the present invention meets: yield strength 550MPa or more, tensile strength 670-830MPa, elongation percentage
>=19%, at 1/4 thickness and 1/2 thickness of -60 DEG C of lower steel plates Charpy-V impact power >=100J, the Z-direction contraction percentage of area >=35%.
The effect of all chemical constituents and its content selection reason are described as follows in the present invention:
C: the intensity of steel is improved with solution strengthening form, influences the essential element of intensity, harden ability and weldability；Carbon content
It is excessively high can toughness to steel and weldability have an adverse effect, carbon content is too low, will lead to that steel plate harden ability is insufficient, and intensity is inclined
It is low.Comprehensively consider, C content range of choice of the present invention is 0.05-0.08%.
Si: improving the intensity of steel with solution strengthening form, and deoxidant element is too low, influences deoxidation effect, it is excessively high can be to table
Face quality, toughness and welding performance have an adverse effect, and comprehensively consider, and Si content range of choice of the present invention is 0.2-0.4%.
Mn: improving the intensity of steel with solution strengthening form, insufficient caused by making up C and reducing, influence intensity, harden ability and
The main alloy element of weldability.It is too low, can not play the role of solution strengthening, it is excessively high the weldability of steel can be generated it is unfavorable
It influences；Meanwhile it being also easy to generate segregation.The range of choice of Mn content of the present invention is 1.41.60%；
Al: deoxidation and fixed nitrogen essential element, there are also the effects of refined crystalline strengthening.The range of choice of Al content of the present invention is
0.02-0.04%。
Nb: there is pinning to strengthen and precipitation strength effect, can fining austenite grains, be conducive to mentioning for intensity and toughness
It is high.The range of choice of Nb content of the present invention is 0.01-0.03%.
V: carbonitride-forming elements improve the intensity and toughness of steel, fining ferrite grains in the form of dispersion-strengtherning
Degree, too high levels can then have an adverse effect to weldability.The range of choice of V content of the present invention is 0.03-0.05%.
Cr: medium carbide former can be improved the harden ability and intensity of steel, make up that C content is lower to lead to intensity
With the deficiency of harden ability decline.Excessive addition, then can low-temperature impact toughness to steel and weldability have an adverse effect.The present invention
The range of choice of Cr content is 0.3-0.5%.
Ni: can improve the intensity of steel simultaneously and improve low-temperature impact toughness, improve the hot cracking tendency of material.Ni content mistake
Gao Shi can generate the higher iron scale of viscosity in continuous casting billet heating process, influence plate surface quality.Ni content of the present invention
Range of choice be 0.6-0.8%.
Mo: can significantly improve the harden ability and intensity of steel, and suitable Mo is added in modifier treatment can overcome steel
Temper brittleness, to improve the impact flexibility of steel.The range of choice of Mo content of the present invention is 0.2-0.4%.
Ti: play the role of precipitation strength by forming TiN, crystal grain can be refined.The range of choice of Ti content of the present invention
For 0.01-0.02%.
B: improving the most significant element of harden ability, excessively high, can have an adverse effect to weldability and low-temperature flexibility.This
The range of choice of invention B content is 0.001-0.002%.
P, S: the major impurity element in steel, it is unfavorable that low-temperature impact toughness and anti-lamellar tearing performance to steel plate can generate
It influences, it is more lower better.According to existing working condition, the range of choice of P, S content of the present invention is P≤0.015%, S≤0.003%.
The manufacturing method of above-mentioned steel plate, includes the following steps
1. raw materials for metallurgy successively through the pretreatment of KR desulfurizing iron, converter top and bottom blowing, LF refining, RH refining and continuous casting, obtains
Thickness is obtained in the continuous casting billet of 300-450mm, covering slow cooling is implemented to continuous casting billet, slow cooling time is 120 hours or more；
2. continuous casting billet is heated to 1170-1250 DEG C, 160-180min is kept the temperature, continuous casting billet is removed after coming out of the stove using high pressure water
Squama；
3. carrying out two-phase control rolling, the first stage is rough rolling step: for start rolling temperature at 1130-1180 DEG C, single pass is average
Reduction ratio >=15%；Second stage is the finish rolling stage: start rolling temperature is 860-900 DEG C, adds up percentage pass reduction >=40%；Heat after rolling
Aligning；
4. steel plate carries out offline covering heap slow cooling, heap slow cooling time >=72 hour after thermal straightening；
5. carrying out quenching+tempering processing to the steel plate after slow cooling, quenching and tempering carry out in continuous oven, hardening heat
It is 890-910 DEG C, time inside furnace 1.8-2.2min/mm；Tempering temperature is 630-680 DEG C, time inside furnace 3.0-4.0min/mm,
Low-carbon bainite air-cooled after coming out of the stove, after can be obtained tempering, different from the high carbon martensite of welding performance difference.
The purpose of this hair invention is to obtain the yield strength 550MPa rank used under the conditions of -60 DEG C easily to weld high-strength height
Flexible steel plate uses the design of low-carbon, low-carbon-equivalent and low crack-sensitivity coefficient contribution, the smelting technique of high purity steel, 300-
The special thick continuous casting steel billet of 450mm takes controlled rolling that the method for modifier treatment is added to produce 70-120mm thickness as raw material
550MPa grades are easily welded the anti-lamellar tearing steel plate of high-strength and high-ductility.
Compared with invention patent publication number CN 102191430A, CN101230444, CN101787489A, the present invention is taken
Ultra-low carbon+a small amount of Ni and Mo ingredient design uses the modifier treatment technique of quenching+tempering in technique, is guaranteeing carbon equivalent
In the case where cooling cracks the susceptible index number (easily welding), bigger thickness steel plate and better low-temperature impact toughness are obtained.From the steel
The specific production stage of plate are as follows: KR molten iron pretreatment-converter-LF refining-RH vacuum outgas-sheet billet continuous casting-slow cooling-rolling-tune
Matter heat treatment-essence inspection-performance detection-is packed and stored.
Compared with the prior art, the advantages of the present invention are as follows:
With invention patent publication number CN 102191430A, CN101230444, CN101787489A technical solution compared with,
Maximum gauge of the present invention reaches 120mm, Charpy-V impact power >=100J under the conditions of -60 DEG C, at the same have low-carbon, low-carbon-equivalent and easily
The characteristics of welding.According to steel plate produced by the invention, on the basis of with good weldability, the production of steel plate is significantly improved
Thickness, maximum gauge is up to 120mm, in addition, steel plate has an excellent high-strength and high-ductility, yield strength >=550MPa, tension is strong
Spend 670-830MPa, elongation percentage >=19%, at 1/4 thickness and 1/2 thickness of -60 DEG C of lower steel plates Charpy-V impact power >=100J, Z
To the contraction percentage of area >=35%, it can satisfy and used under -60 DEG C of cryogenic conditions.
Detailed description of the invention
Fig. 1 is the micro-organization chart of the 70mm thickness steel plate of the embodiment of the present invention 1；
Fig. 2 is the micro-organization chart of the 120mm thickness steel plate of the embodiment of the present invention 2.
Specific embodiment
The present invention will be described in further detail below with reference to the embodiments of the drawings.
The manufacturing method of special thick easily welding steel of the invention, process flow: KR molten iron pretreatment-converter smelting-LF essence
Refining-RH vacuum outgas-continuous casting-continuous casting billet covering slow cooling-continuous casting billet inspection cleaning-slab heating-high-pressure water descaling-
The techniques such as rolling-aligning-steel plate heap slow cooling-quenching-tempering, finished product thickness are the steel plate of 70mm and 120mm.
Above-mentioned heating, rolling and slow cooling stage specifically comprises the processes of: 370mm thickness continuous casting billet is heated to 1180-1200
DEG C, keep the temperature 180min(Examples 1 and 2), continuous casting billet uses high-pressure water descaling after coming out of the stove；Then two-phase control rolling is carried out: first
1100-1150 DEG C of stage start rolling temperature (Examples 1 and 2), workpiece thickness 170mm(example 1) or 200mm(example 2), single track
Secondary average reduction ratio 16.5%(example 1) or 15.5%(example 2)；Second stage start rolling temperature is 850 DEG C, adds up percentage pass reduction
58.8%(embodiment 1) or 860 DEG C of second stage start rolling temperature, add up percentage pass reduction 40%(embodiment 2), final steel plate thickness
For 70mm(embodiment 1) and 120mm(embodiment 2).Roll rear thermal straightening；Steel plate carries out offline heap slow cooling, heap slow cooling after thermal straightening
Time 72 hours (embodiment 1) and 84 hours (embodiment 2).
Steel plate after the completion of slow cooling enters continuous oven and is quenched.Embodiment 1: 890 DEG C of heating temperature, time inside furnace
1.8min/mm uses quenching press water quenching.Embodiment 2: 910 DEG C of heating temperature, time inside furnace 1.8min/mm uses quenching press water
It quenches.Tempering is carried out in continuous oven to the steel plate for completing quenching treatment.Embodiment 1: 660 DEG C of heating temperature, time inside furnace
3.0min/mm, embodiment 2: 640 DEG C of heating temperature, time inside furnace 4.0min/mm.
The chemical component that Examples 1 and 2 correspond to steel plate is shown in Table 1, and the mechanical property of steel plate is shown in Table 2, the microscopic structure of steel plate
It is as depicted in figs. 1 and 2 respectively.
The chemical component (wt.%) of the anti-lamellar tearing steel plate of high-strength and high-ductility is easily welded in 1 Examples 1 and 2 of table
| Example | C | Si | Mn | P | S | Al | Nb | V | Ti | Cr | Ni | Mo | B | N | Ceq | Pcm |
| 1 | 0.07 | 0.25 | 1.48 | 0.008 | 0.0009 | 0.031 | 0.016 | 0.033 | 0.016 | 0.38 | 0.68 | 0.26 | 0.0011 | 0.0036 | 0.50 | 0.21 |
| 2 | 0.08 | 0.26 | 1.52 | 0.008 | 0.0008 | 0.032 | 0.018 | 0.036 | 0.015 | 0.37 | 0.67 | 0.25 | 0.0012 | 0.0034 | 0.51 | 0.22 |
Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15
Pcm=C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B
The mechanical property of the anti-lamellar tearing steel plate of high-strength and high-ductility is easily welded in 2 Examples 1 and 2 of table
Claims (3)
1. a kind of 550MPa grades special thick easily welding anti-lamellar tearing steel plate of high tenacity, it is characterised in that: the steel plate is using Fe as base
Plinth element, and include the chemical component of following mass percent: C 0.05-0.08%, Si 0.2-0.4%, Mn 1.4-
1.6%, Al 0.02-0.04%, Nb 0.01-0.03%, V 0.03-0.05%, Cr 0.3-0.5%, Ni 0.6-0.8%,
Mo 0.2-0.4%, Ti 0.01-0.02%, B 0.001-0.002%, P≤0.015%, S≤0.003%, N≤0.007%,
Carbon equivalent≤0.55, surplus are inevitable impurity, weld crack sensitivity coefficient Pcm=C+Si/30+ (Mn+Cu+Cr)/20+
Ni/60+Mo/15+V/10+5B≤0.24, steel plate with a thickness of 70-120mm；The mechanical property of steel plate meets: yield strength
550MPa or more, tensile strength 670-830MPa, elongation percentage >=19%, summer at 1/4 thickness and 1/2 thickness of -60 DEG C of lower steel plates
>=100J more equal than ballistic work, the Z-direction contraction percentage of area >=35%.
2. the method for the 550MPa grades of special thick easily welding anti-lamellar tearing steel plates of high tenacity, special described in a kind of manufacturing claims 1
Sign is: including the following steps
1. raw materials for metallurgy successively through the pretreatment of KR desulfurizing iron, converter top and bottom blowing, LF refining, RH refining and continuous casting, obtains thick
The continuous casting billet in 300-450mm is spent, covering slow cooling is implemented to continuous casting billet, slow cooling time is 120 hours or more；
2. continuous casting billet is heated to 1170-1250 DEG C, 160-180min is kept the temperature, continuous casting billet uses high-pressure water descaling after coming out of the stove；
3. carrying out two-phase control rolling, the first stage is rough rolling step: start rolling temperature is under 1130-1180 DEG C, single pass mean pressure
Rate >=15%；Second stage is the finish rolling stage: start rolling temperature is 860-900 DEG C, adds up percentage pass reduction >=40%；Heat is rectified after rolling
Directly；
4. steel plate carries out offline covering heap slow cooling, heap slow cooling time >=72 hour after thermal straightening；
5. carrying out quenching+tempering processing to the steel plate after slow cooling, quenching and tempering carry out in continuous oven, and hardening heat is
890-910 DEG C, time inside furnace 1.8-2.2min/mm；Tempering temperature is 630-680 DEG C, time inside furnace 3.0-4.0min/mm, out
It is air-cooled after furnace.
3. the manufacturing method of the 550MPa grades according to claim 2 special thick easily welding anti-lamellar tearing steel plate of high tenacity,
It is characterized in that: obtaining the steel plate of low-carbon bainite tissue after the tempering.
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| CN107904488B (en) * | 2017-11-06 | 2020-02-07 | 江阴兴澄特种钢铁有限公司 | Super-thick high-strength high-toughness lamellar tearing-resistant Q550 steel plate and manufacturing method thereof |
| CN112048675A (en) * | 2020-07-30 | 2020-12-08 | 江阴兴澄特种钢铁有限公司 | Low-yield-ratio granular bainite high-strength steel plate used in low-temperature environment and manufacturing method thereof |
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| CN115029633A (en) * | 2022-06-21 | 2022-09-09 | 湖南华菱湘潭钢铁有限公司 | Multi-process adaptive Q550 medium-thickness steel plate and production method thereof |
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| CN115141968A (en) * | 2022-07-28 | 2022-10-04 | 湖南华菱湘潭钢铁有限公司 | Production method of quenched and tempered steel plate for Q620-level high-corrosion-resistance high-strength offshore structure |
| CN116254464A (en) * | 2022-11-25 | 2023-06-13 | 江阴兴澄特种钢铁有限公司 | Heat-resistant steel plate with thickness exceeding 120mm and manufacturing method thereof |
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